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46 巻, 6 号
選択された号の論文の14件中1～14を表示しています
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浅田 長平1960 年 46 巻 6 号 p. 641-642
発行日: 1960/06/01
公開日: 2010/10/12
ジャーナル オープンアクセスPDF形式でダウンロード (546K) -
高炉の炭素および熱量的検討-I八塚 健夫, 沢村 惇, 太田 奨, 福田 隆博1960 年 46 巻 6 号 p. 643-652
発行日: 1960/06/01
公開日: 2010/10/12
ジャーナル オープンアクセスThe consumption of carbon and the heat in an operating blast furnace constitutes a basic factor for a theoretical evaluation of the pig-iron manufacturing operation, together with the material consumption.
This report gives the result of studying how the carbon consumption is performed in each part of a blast furnace, how the calory thus generated is distributed and to what extent the calory consumption of charged materials will amount, referring also to the application of those results to the blast furnace operation based on the studies from both theoretical and practical aspects.抄録全体を表示PDF形式でダウンロード (2237K) -
中井 弘1960 年 46 巻 6 号 p. 652-657
発行日: 1960/06/01
公開日: 2010/10/12
ジャーナル オープンアクセスExperiments on the sulphurization of cast iron in H2S gas current at high temperatures were conducted and the following results were obtained.
(1) The sulphurization product of cast iron was composed of pyrrhotite Fe1-xS and pyrite FeS2, which were the same as those of iron and steel. In the outer layer of sulphurization product, carbon and phosphor didn't diffuse, on the contrary manganese diffused freely, silicon did a little.
(2) The sulphurization rate was controlled by the parabolic rate law, and the following formula was obtained:
W2=1.15×10-6t
W: sulphurization rate, g/cm2
t: sulphurization time's
(3) Between the sulphurization rate and temperature, the exponential law was found and the following formula was obtained.
K=10-2·e-33500/RT
K: sulphurization rate constant, (g/cm2) 2/s
R: gas constant
T: sulphurization temperature, °K
(4) The structure of cast iron did not affect the sulphurization rate.
(5) Carbon expedited the sulphurization rate of cast iron, on the contrary silicon and manganese did not expedite it.抄録全体を表示PDF形式でダウンロード (2505K) -
関口 春次郎, 稲垣 道夫1960 年 46 巻 6 号 p. 657-665
発行日: 1960/06/01
公開日: 2010/10/12
ジャーナル オープンアクセスThe authors performed a series of researches on continuous cooling transformation diagrams of structural steels used for welding and reported them successively in Journal of Japan Welding Society (1957-1959, vols. 26-28). In these reports, the continuous cooling transformation diagrams were obtained with small specimens in the case of rapid-heating to maximum temp. 1350°C, cooling by various processes immediately after reaching its temp. and without holding at its temp. They gave fundamental data for tha sake of selecting the weldable steels and determined the conditions when welding these steels. Therefore, such continuous cooling transformation diagrams were presumed very important and useful.
In the hresent report, on the basis of the results of the above researches, further determinations were made on the continuous cooling transformation diagrams for high tensile steels 2H which were of Mn-Si type and showed the tensile strength enhanced to about 60kg/mm2 by the heat-treatment of water-quenching and tempering.
For those 2H steels could be adopted also, a diagram that was plotted to show the relation between critical cooling-time Cz', Cf' or 50% martensite cooling-time and the carbon equivalent of mild steels and Mn-Si type high tensile steels as rolled or normalized. And then, using this diagram the critical cooling-time Cz', Cf' and 50% martensite cooling-time and the carbon equivalent were determined with mild steels and Mn-Si type high tensile steels as rolled or normalized And then, based on this diagram the critical cooling-time Cz', Cf' and 50% martensite cooling times of arbitrary steel grades could be predicted from the carbon equivalent Ceq= (C+1/12Mn+1/24Si) % of those steels.
Next, the various types of high tensile steel having 60kg/mm2 tensile strengths were compared with each other, From stand points of the buctility and crack-sensitivity of the weld heat affected zone, the critical cooling-time Cf' which began to reveal existance of primary ferrite was important, and the steels having smaller value of Cf' were found desirable. For this purpose, even with any type of steels, it was necessary that the carbon content of a steel was lowered to a mimimum.抄録全体を表示PDF形式でダウンロード (4982K) -
オーステナイト高Mn鋼の研究-I今井 勇之進, 斎藤 利生1960 年 46 巻 6 号 p. 665-673
発行日: 1960/06/01
公開日: 2010/10/12
ジャーナル オープンアクセスAustenite高Mn鋼の溶体化処理後の再加熱によるcarbide析出について研究するため, 先ずstandardのHadfield鋼について恒温加熱および連続加熱間におけるcarbideの析出および析出物の形態について実験し, 以下の結果を得た.
1. 溶体化処理後の恒温加熱におけるcarbideの析出は, 650～700℃付近を頂点とするC-曲線として現わされ, P.C. の析出は約600℃を頂点とする同じくC-曲線で現わされる.
2. 折出物の形態は, 析出の初期はaustenite粒界におけるcarbide filmの形成であるが, 低温域ではcarbide filmの形成が遅く, 粒界から結晶の劈開面に沿う針状析出を生ずる. 高温域ではcarbide filmの形成に引続き, 粒界におけるcarbide filmの粒状化, 粒状carbideの成長と凝集が順次に起る.
3. P.C. の核生成は約600℃でもつとも早いが, 以後のP.C. の成長はさらに温度の低いほどいちじるしく, 500℃付近で最大の成長速度を有するものとみられる.
4. 析出したP.C. は高倍率で識別し得る微細なlamellar pearlite状の形態をとり, 低温度で析出するP.C. ほどlamellaeの間隔が小さい.
5. 加熱間における析出は, 加熱速度の速いほど析出温度が高温側に移行しかつ析出量も少なくなる. 約15℃/mnの加熱ではP.C. は現われず, また約45℃/mn以上の速度ではcarbideの析出も避け得ることが推定される.
6. 機械的性質は板状carbideの析出し始める350℃付近から低下し始め, 抗張力はcarbide filmのもっとも成長し易い750℃付近で最低値をとり, また衝撃値, 伸び, 絞りはP.C. の析出域で最低値をとる. carbide析出による硬度増加は主として板状carbideが影響している.抄録全体を表示PDF形式でダウンロード (5417K) -
Ni基耐熱合金に関する研究-VII長谷川 太郎, 落合 治1960 年 46 巻 6 号 p. 673-677
発行日: 1960/06/01
公開日: 2010/10/12
ジャーナル オープンアクセスEffects of Ti, Al, C and Mo contents on stress-rupture properties of alloy M252 were investigated.
There seemed to be a peak stress-rupture life at 1.2% Al when Ti was 3.1%, and stress-rupture life was decreased in the case of specimens containing over 1.2% Al. Ti+Al atm. %=6.5 gave the peak of stress-rupture and creep ductility.
Effect of Ti and Al on stress-rupture characteristics was clear in the case of heat treatment B (1065°C×8h W.Q., 800°C×2.5h A.C. and 700°C×18h A.C.) but it was not clear in the case of heat treatment G (1065°C×8h. A.C., 760°C×15h. A.C.).
Carbon did not affect the short-time stress-rupture test, but it did so in the long time stress rupture test, and stress rupture life was decreased by the increase of carbon. Hardness after heat treatment was increased by carbon and nitrogen, but it seemed that overaging at high temperature was promoted by them and the decrease of long time stress rupture life was affected by overaging.
Ultimate strength of short-time tensile test between room temperature and 750°C, and stress-rupture strength less than 500 hours of the alloy containing 11% Mo was higher than those of the alloy containing 10% Mo. But strength was not increased by increasing Mo content up to 15%, although these values were higher than the alloy containing 10% Mo. The effect of Mo on increasing strength of alloy was not clear in the case of testing temperature of 816 and 850°C.
There was no embrittling effect by increasing Mo content in these test. But the net work which precipitates at grain boundaries was increased by heating 11% Mo alloy for 1000 hours at 850°C, and it lowered Charpy's impact value.
The resistance to oxidation in the air below 900°C was good enough, and it was not affected by increasing the Mo content.抄録全体を表示PDF形式でダウンロード (1084K) -
前川 静弥, 米山 善夫1960 年 46 巻 6 号 p. 678-682
発行日: 1960/06/01
公開日: 2010/10/12
ジャーナル オープンアクセスIn case of trying to decompose sulphide in basic slags by means of the electric resistance heating furnace, the authors have sometimes failed to release and recover it as SO2. It took a many time especially the high basic sample because of the strong affinity of sulphur to its matrix. So, they used the high frequency induction heating combustion apparatus to decompose the sample with pure iron in O2 flow. Consequently, sulphur was completely decomposed and released in the flow out gas, as SO2, which was absorbed into H2O and caught as H2SO3.
Then, HC1 and starch solution were added in the absorbed water and titrated by M/1000 KIO3.
The influence of pH, aquous temperature, combustion time and O2 flow upon SO2 yields were also examined. The combustion was over in 3mn. and 94% of sulphur was recovered with the aid of one absorption bottle, and 97%, two bottles. The authors examined the behavior of sulphur on the synthetic sample prepared by sulphide, sulphate and etc., and comfirmed that even high contents sample of 1% sulphur could be recovered almost stoichiometrically.
Analytical time is about 8mn. for one sample.抄録全体を表示PDF形式でダウンロード (1036K) -
森永 孝三1960 年 46 巻 6 号 p. 683-700
発行日: 1960/06/01
公開日: 2010/10/12
ジャーナル オープンアクセスPDF形式でダウンロード (4711K) -
Herbert Briefs1960 年 46 巻 6 号 p. 701-710
発行日: 1960/06/01
公開日: 2010/10/12
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将来の鉄鋼研究体制について1960 年 46 巻 6 号 p. 711-721
発行日: 1960/06/01
公開日: 2010/12/22
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1960 年 46 巻 6 号 p. 722-726,622
発行日: 1960/06/01
公開日: 2010/12/22
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1960 年 46 巻 6 号 p. 727-730
発行日: 1960/06/01
公開日: 2010/10/12
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1960 年 46 巻 6 号 p. 731-732
発行日: 1960/06/01
公開日: 2010/10/12
ジャーナル オープンアクセスPDF形式でダウンロード (698K) -
1960 年 46 巻 6 号 p. 735-736
発行日: 1960/06/01
公開日: 2010/10/12
ジャーナル オープンアクセスPDF形式でダウンロード (609K)
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